Methods for producing perovskite halide films

ABSTRACT

An aspect of the present disclosure is a method that includes exchanging at least a portion of a first cation of a perovskite solid with a second cation, where the exchanging is performed by exposing the perovskite solid to a precursor of the second cation, such that the precursor of the second cation oxidizes to form the second cation and the first cation reduces to form a precursor of the first cation.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims priority to U.S. Non-provisional patent application Ser. No. 15/437,779 and U.S. Provisional Application No. 62/298,079 filed Feb. 21, 2017 and Feb. 22, 2016, respectively, the contents of which are incorporated herein by reference in their entirety.

CONTRACTUAL ORIGIN

The United States Government has rights in this disclosure under Contract No. DE-AC36-08GO28308 between the United States Department of Energy and Alliance for Sustainable Energy, LLC, the Manager and Operator of the National Renewable Energy Laboratory.

BACKGROUND

α-HC(NH₂)₂PbI₃ (α-FAPbI₃) perovskite films are highly desirable for perovskite solar cells (PSCs) due to their enhanced sunlight absorption extending into the infrared (IR). However, the thin-film deposition of (α-FAPbI₃) perovskite is significantly more challenging compared to its CH₃NH₃PbI₃ (MAPbI₃) perovskite counterpart.

Films of organolead trihalide perovskites have been studied extensively as light-absorbing materials, which are at the heart of the new perovskite solar cells (PSCs). The unique combination of low-cost solution-processing, and high power-conversion efficiencies (PCEs) rivaling those of conventional Si-based solar cells, holds great promise for PSCs. While methylammonium lead triiodide (CH₃NH₃PbI₃ or MAPbI₃) perovskite, with a bandgap of ˜1.55 eV, is the most widely studied in the context of PSCs, formamidinium lead triiodide (α-HC(NH₂)₂PbI₃ or α-FAPbI₃) perovskite for PSCs is also very promising. This is primarily because FAPbI₃ has a smaller band gap of ˜1.45 eV, extending light absorption into the infrared region of the solar spectrum.

Since the morphology of perovskite films plays a central role in determining the PCE of PSCs, unprecedented efforts have been made in order to control the film uniformity and/or tailor the perovskite microstructures, with particular emphasis on MAPbI₃ perovskite. However, the development of effective protocols for the engineering of FAPbI₃ perovskite film morphologies and microstructures are lagging due to the following challenges. First, the ‘ionic radius’ of FA⁺ cation (2.79 Å) is larger than that of MA⁺ cation (2.70 Å), and the molecular structures of FA⁺ and MA⁺ cations are quite different, both of which are expected to affect solution-growth kinetics of α-FAPbI₃ perovskite. Second, FAPbI₃ also crystallizes in a ‘yellow’ δ-FAPbI₃ non-perovskite polymorph at room temperature, which is associated with the formation of the α-FAPbI₃ perovskite. Therefore, the growth of phase-pure α-FAPbI₃ perovskite films requires stricter control over the synthetic procedures compared with MAPbI₃, which is a major hurdle in the path of realizing the full potential of α-FAPbI₃ perovskite for PSCs. Thus, there is a need for methods that overcome these difficulties to produce high quality α-FAPbI₃ perovskite films suitable for PSCs.

SUMMARY

An aspect of the present disclosure is a method that includes exchanging at least a portion of a first cation of a perovskite solid with a second cation, where the exchanging is performed by exposing the perovskite solid to a precursor of the second cation, such that the precursor of the second cation oxidizes to form the second cation and the first cation reduces to form a precursor of the first cation. In some embodiments of the present disclosure, the exchanging may be performed by exposing the perovskite solid to a gas that includes the precursor of the second cation. In some embodiments of the present disclosure, the exposing may be performed with the gas at a pressure between about 0.1 atmospheres and about 5 atmospheres. In some embodiments of the present disclosure, the exchanging may be performed at a temperature between 100° C. and 300° C. In some embodiments of the present disclosure, the perovskite solid may include at least one of a particle and/or a film.

In some embodiments of the present disclosure, the perovskite solid may be defined by ABX₃, where A includes at least one of the first cation or the second cation, B includes a third cation, and X includes an anion. In some embodiments of the present disclosure, the first cation may include methylammonium. In some embodiments of the present disclosure, the second cation may include at least one of formamidinium, guanidinium, acetamidinium, and/or ethylammonium. In some embodiments of the present disclosure, the second cation may include formamidinium. In some embodiments of the present disclosure, the third cation may include a metal in the 2+ valence state. In some embodiments of the present disclosure, the metal may include at least one of lead, tin, and/or germanium. In some embodiments of the present disclosure, the anion may include a halogen. In some embodiments of the present disclosure, the halogen may include at least one of fluorine, chlorine, bromine, and/or iodine.

In some embodiments of the present disclosure, the precursor of the second cation may include at least one of formylimidamide, guanidine, acetamidine, and/or ethylamine. In some embodiments of the present disclosure, the precursor of the first cation may include methylammonia. In some embodiments of the present disclosure, the perovskite solid may be converted from methylammonium lead triiodide to formamidinium lead triiodide. In some embodiments of the present disclosure, the method may further include, prior to the exchanging, forming the perovskite solid by at least one of a solution deposition method and/or a vapor deposition method. In some embodiments of the present disclosure, the method may further include, producing the gas by reacting a salt-precursor of the precursor of the second cation with a hydroxide salt. In some embodiments of the present disclosure, the salt-precursor of the precursor of the second cation may include formamidine acetate. In some embodiments of the present disclosure, the hydroxide salt may include sodium hydroxide.

An aspect of the present disclosure is a device that includes a film of formamidinium lead triiodide, where the formamidinium lead triiodide has a short-circuit density of greater than 22.0 mA/cm². In some embodiments of the present disclosure, the film may have thickness between 10 nm and 3 μm. In some embodiments of the present disclosure, the device may further include a substrate, where the film is in physical contact with the substrate. In some embodiments of the present disclosure, the substrate may include at least one of at least one of a transparent conducting oxide, a glass, a metal foil, and/or a plastic. In some embodiments of the present disclosure, the device may have a power-conversion efficiency of greater than 17%.

REFERENCE NUMERALS

100 perovskite 110 A-cation 120 B-cation 130 anion (X) 200 exchange process 210 cation precursor 300 method 310 forming 320 exchanging 700 system 710 hotplate 720 substrate 730 MAPbI₃ perovskite film/α-FAPbI₃ perovskite film 740 CaO dryer 750 FA(Ac) + NaOH 760 box

BRIEF DESCRIPTION OF THE DRAWINGS

Exemplary embodiments are illustrated in referenced figures of the drawings. It is intended that the embodiments and figures disclosed herein are to be considered illustrative rather than limiting.

FIG. 1 illustrates the structure of a perovskite, according to some embodiments of the present disclosure.

FIG. 2 illustrates an exchange process for converting a first perovskite to a second perovskite, according to some embodiments of the present disclosure.

FIG. 3 illustrates a method for converting a first perovskite to a second perovskite, according to some embodiments of the present disclosure.

FIG. 4A illustrates X-ray diffraction (XRD) patterns of formylimidamide-gas-treated (150° C.) films for t=0 to 4 min, according to some embodiments of the present disclosure. (A). The vertical dashed lines mark the peak positions of MAPbI₃ perovskite.

FIG. 4B illustrates higher-resolution XRD patterns (overlaid) of films corresponding to those shown in FIG. 4A. Vertical dashed lines mark the MAPbI₃ (220) and α-FAPbI₃ (200) perovskite peak positions, respectively.

FIG. 4C illustrates optical absorption spectra of the formylimidamide-gas-treated (150° C./) films for t=0 to 4 min, according to some embodiments of the present disclosure.

FIG. 4D illustrates higher resolution optical absorption spectra for the dashed rectangle shown in FIG. 4C.

FIG. 5 illustrates experimental data obtained, according to some embodiments of the present disclosure. Panels A and B show scanning electron microscope (SEM) micrographs of perovskite films: (Panel A) MAPbI₃ and (Panel B) α-FAPbI₃. Panels C and D show cross-section SEM micrographs of PSCs made from perovskites: (Panel C) MAPbI₃ and (Panel D) α-FAPbI₃. The different PSC layers are marked.

FIG. 6A illustrates current density (J)-voltage (V) J-V curve from the best α-FAPbI₃-based PSC (inset: PV performance parameters), according to some embodiments of the present disclosure.

FIG. 6B illustrates the corresponding external quantum efficiency (EQE) response for current density data of FIG. 6A, according to some embodiments of the present disclosure.

FIG. 7 illustrates a schematic of a system for the generation of H₂N—CH═NH (formylimidamide) gas, and the treatment of MAPbI₃ film for its conversion to α-FAPbI₃ film, according to some embodiments of the present disclosure.

FIG. 8 illustrates the evolution of absorption spectra of perovskite structures from MAPbI₃ to FAPbI₃ as a function of aminium displacement (AD) reaction time, according to some embodiments of the present disclosure.

DETAILED DESCRIPTION

The present disclosure may address one or more of the problems and deficiencies of the prior art discussed above. However, it is contemplated that some embodiments as disclosed herein may prove useful in addressing other problems and deficiencies in a number of technical areas. Therefore, the embodiments described herein should not necessarily be construed as limited to addressing any of the particular problems or deficiencies discussed herein.

FIG. 1 illustrates that a perovskite may organize into cubic crystalline structures and may be described by the general formula ABX₃, where X (130) is an anion and A (110) and B (120) are cations, typically of different sizes with the A-cation 110 typically larger than the B-cation 120. In a cubic unit cell, the B-cation 120 resides at the eight corners of a cube, while the A-cation 110 is located at the center of the cube and is surrounded by twelve X-anions 130 centrally located between B-cations 120 along each edge of the cell. Typical inorganic perovskites include calcium titanium oxide (calcium titanate) minerals such as, for example, CaTiO₃ and SrTiO₃. In some embodiments of the present invention, the A-cation 110 may include a nitrogen-containing organic compound such as an alkyl ammonium compound. The B-cation 120 may include a metal and the anion 130 may include a halogen.

Additional examples for an A-cation A 110 include organic cations and/or inorganic cations. A-cations 110 may be an alkyl ammonium cation, for example a C₁₋₂₀ alkyl ammonium cation, a C₁₋₆ alkyl ammonium cation, a C₂₋₆ alkyl ammonium cation, a C₁₋₅ alkyl ammonium cation, a C₁₋₄ alkyl ammonium cation, a C₁₋₃ alkyl ammonium cation, a C₁₋₂ alkyl ammonium cation, and/or a C₁ alkyl ammonium cation. Further examples of organic A-cations 110 include methylammonium (CH₃NH³⁺), ethylammonium (CH₃CH₂NH³⁺), propylammonium (CH₃CH₂CH₂NH³⁺), butylammonium (CH₃CH₂ CH₂ CH₂NH³⁺), formamidinium (NH₂CH═NH²⁺), and/or any other suitable nitrogen-containing organic compound. In other examples, an A-cation 110 may include an alkylamine. Thus, an A-cation 110 may include an organic component with one or more amine groups. For example, an A-cation 110 may be an alkyl diamine halide such as formamidinium (CH(NH₂)₂)⁺.

Examples of metal B-cations 120 include, for example, lead, tin, germanium, and or any other 2+ valence state metal that can charge-balance the perovskite 100. Examples for the anion 130 include halogens: e.g. fluorine, chlorine, bromine, iodine and/or astatine. In some cases, a perovskite 100 may include more than one anion 130, for example pairs of halogens; chlorine and iodine, bromine and iodine, and/or any other suitable pairing of halogens. In other cases, the perovskite 100 may include two or more halogens of fluorine, chlorine, bromine, iodine, and/or astatine.

Thus, the A-cation 110, the B-cation 120, and the anion 130 (X) may be selected within the general formula of ABX₃ to produce a wide variety of perovskites 100, including, for example, methylammonium lead triiodide (CH₃NH₃PbI₃), and mixed halide perovskites such as CH₃NH₃PbI_(3-x)Cl_(x) and CH₃NH₃PbI_(3-x)Br_(x). Thus, a perovskite 100 may have more than one halogen element, where the various halogen elements are present in none integer quantities; e.g. x is not equal to 1, 2, or 3. In addition, perovskite halides, like other organic-inorganic perovskites, can form three-dimensional (3-D), two-dimensional (2-D), one-dimensional (1-D) or zero-dimensional (0-D) networks, possessing the same unit structure.

As stated above, the A-cation 110 may include an organic constituent in combination with a nitrogen constituent. In some cases, the organic constituent may be an alkyl group such as straight-chain and/or branched saturated hydrocarbon group having from 1 to 20 carbon atoms. In some embodiments, an alkyl group may have from 1 to 6 carbon atoms. Examples of alkyl groups include methyl (C₁), ethyl (C₂), n-propyl (C₃), isopropyl (C₃), n-butyl (C₄), tert-butyl (C₄), sec-butyl (C₄), iso-butyl (C₄), n-pentyl (C₅), 3-pentanyl (C₅), amyl (C₅), neopentyl (C₅), 3-methyl-2-butanyl (C₅), tertiary amyl (C₅), and n-hexyl (C₆). Additional examples of alkyl groups include n-heptyl (C₇), n-octyl (C₈) and the like.

FIG. 2 illustrates an exchange process 200 for converting a first perovskite 100A having a first A-cation 110A to a second perovskite 100B having a second A-cation 110B by exposing the first perovskite 100A to a precursor of the second A-cation 110B, referred to herein as the second cation precursor 210B. The exposing results in the second cation precursor 210B being oxidized to produce the second A-cation 110B, and the first A-cation 110B being reduced to produce a precursor of the first A-cation 110A, referred to herein as the first cation precursor 201A. In addition, the exposing of the first perovskite 100A to the second cation precursor 210 triggers the exchange process 200 in which the first A-cation 110A is exchanged with the second A-cation 110B, with the expulsion of the first cation precursor 210A from the first perovskite 100A to form the second perovskite 100B. Thus, the exchange process 200 may be performed with the first perovskite 100A and the second perovskite 100B in solid crystalline phases, for example, as films and/or particles and by exposing the first perovskite 100A to the second cation precursor 210B in the gas phase. According to some embodiments of the present disclosure, the first perovskite 100A may be a MAPbI₃ perovskite film, the second perovskite 100B may be an α-FAPbI₃ perovskite film, such that the first A-cation 110A is methyl ammonium, the first cation precursor 210A is methyl ammonia, the second A-cation 110B is formamidinium, and the second cation precursor 210B is formylimidamide.

FIG. 3 illustrates a method 300 for converting a first perovskite 100A to a second perovskite 100B according to the exchange process (not shown) described above for FIG. 2, according to some embodiments of the present disclosure. The method 300 may begin with the forming 310 of a first perovskite 100A, where the forming 310 may be achieved by solution and annealing methods as described below. In some embodiments, the forming 310 may result in a first perovskite 100A that is a MAPbI₃ perovskite film. The first perovskite 100A may then be converted to a second perovskite 100B by an exchanging 320 of the A-cation (not shown) of the first perovskite 100A with the A-cation (not shown) of the second perovskite 100B. For example, as described above, a first perovskite 100A of a MAPbI₃ perovskite film may be converted to a second perovskite 100B of an α-FAPbI₃ perovskite film by exchanging 320 a first A-cation of methyl ammonium (not shown) of the first perovskite 100A with a second A-cation of formamidinium (not shown) of the second perovskite 100B. The exchanging 320 may be accomplished by exposing the first perovskite 100A to a precursor of the second cation, referred to herein as the second cation precursor 210B, such that the exchanging 320 produces the second perovskite 100B and the first cation precursor 200A, for example methyl ammonia.

Thus, some embodiments of the present disclosure relate to solvent-free, irreversible methods for converting methylammonium lead iodide (MAPbI₃) perovskite films to formamidinium lead triiodide (α-HC(NH₂)₂PbI₃ or α-FAPbI₃) perovskite films while preserving the high-quality morphology of the original MAPbI₃ perovskite films. This approach may entail exposing a starting MAPbI₃ perovskite film to H₂N—CH═NH (formylimidamide) gas at elevated temperatures, for example at about 150° C., for a period of time, for example about 4 minutes, which results in an efficient cation-displacement redox reaction and a morphology-preserving conversion of the starting MAPbI₃ perovskite film to a α-FAPbI₃ perovskite film. Insights into the mechanisms responsible for the success of this gas-based approach are provided below. In addition, high-efficiency perovskite solar cells (PSCs) fabricated from the resultant α-FAPbI₃ perovskite films confirm the efficacy of this approach in preserving the high-quality morphology of the original MAPbI₃ perovskite films.

As shown schematically in FIG. 2, exposing an as-deposited, smooth MAPbI₃ perovskite film to gaseous H₂N—CH═NH (formylimidamide) (150° C., 5 min) resulted in the conversion of the MAPbI₃ film to an α-FAPbI₃ film. As described above, the exchange process for converting the MAPbI₃ film to the α-FAPbI₃ film involved reaction (1) below, which includes the reduction (proton donation) of CH₃NH₃ ⁺ (methylammonium) into neutral CH₃NH₂ (methylammonia), and the oxidation (proton acceptance) of neutral H₂N—CH═NH (formylimidamide) into H₂N—CH═NH₂+(formamidinium):

(CH₃NH₃)PbI₃(s)+H₂N—CH═NH(g)→α-(H₂N—CH═NH₂)PbI₃(s)+CH₃NH₂(g)  (1).

FIGS. 4A and 4B plot X-ray diffraction (XRD) patterns showing the progression of reaction (1) at t=˜1, 2, 3, and 4 minutes of formylimidamide treatment at about 150° C. A gradual shift of the peaks to lower 20 was observed in FIG. 2A. FIG. 2B shows the details of the XRD patterns in the 20 range 27.50° to 29.00°. The presence of phase-pure MAPbI₃ perovskite at t=0 min was confirmed by the presence of the 220 reflection at 2θ=28.42°. With exposure to formylimidamide gas, the FAPbI₃ perovskite 200 reflection started to appear centered around 2θ=28.10°. With increasing formylimidamide treatment duration, the intensity of the α-FAPbI₃ perovskite 200 reflection increased, at the expense of the MAPbI₃ 220 reflection. At t=4 min, the MAPbI₃→α-FAPbI₃ conversion was complete. Since the α-FAPbI₃ perovskite phase is thermodynamically stable at 150° C., the formation of the undesirable ‘yellow’ δ-FAPbI₃ non-perovskite phase during reaction (1) was apparently completely suppressed.

It should be noted that although the method describe above utilizes formylimidamide, other compounds such as guanidine/guadinium cation (HNC(NH₂)₂→C(NH₂)₃ ⁺), acetamidine/acetamidinium cation (CH₃CHNHNH₂→CH₃CH(NH₂)₂), and/or ethylamine/ethylammonium cation (CH₃CH₂NH₂→CH₃CH₂NH₃ ⁺) may also achieve the same effects achieved by formylimidamide, resulting in final perovskite films such as guanidinium lead triiodide, acetamidinium lead triiodide, and/or ethylammonium lead triiodide. For example, a MAPbI₃ perovskite film may be exposed to guanidine to produce a guanidinium lead triiodide perovskite film, a MAPbI₃ perovskite film may be exposed to acetamidine to produce an acetamidinium lead triiodide perovskite film, and/or a MAPbI₃ perovskite film may be exposed to ethylamine to produce an ethylammonium lead triiodide perovskite film. In addition, although the displacement reaction illustrated above in reaction (1) may be irreversible any the perovskite films produced may be converted a second time (or more) by subsequent reactions with a different displacement compound. For example, a formamidinium lead triiodide perovskite film may be converted to a guanidinium lead triiodide perovskite film by exposing the formamidinium lead triiodide perovskite film to guanidine. Or a guanidinium lead triiodide perovskite film may be converted to an acetamidinium lead triiodide perovskite film by exposing the guanidinium lead triiodide perovskite film to acetamidine.

FIGS. 4C and 4D show optical-absorption spectra for the films at t=˜1, 2, 3, and 4 minutes of formylimidamide gas treatment at about 150° C., corresponding to the XRD patterns in FIGS. 4A and 4B. While the absorbance at low wavelengths in all the films was virtually indistinguishable, at longer wavelengths the extension of absorbance into IR is clearly seen in FIG. 4C. FIG. 4D shows details of the absorption spectra in the IR range, where the absorption was extended by ˜30 nm into the IR. Thus, the XRD and the optical absorption data confirm the feasibility of the MAPbI₃→α-FAPbI₃ phase conversion phase conversion using the formylimidamide-gas treatment.

FIG. 5, Panels A and B are top-view SEM images of MAPbI₃ and α-FAPbI₃ perovskite films (after t=˜4 minutes formylimidamide-gas-treatment at about 150° C.), respectively. The dense, full-coverage MAPbI₃ perovskite film in Panel A of FIG. 5 was deposited where the uniform morphology of that film is clearly evident. Most remarkably, the same uniform morphology was maintained in the converted α-FAPbI₃ perovskite film, as seen in Panel B of FIG. 5. Panels C and D of FIG. 5 show cross-sectional SEM morphologies of the MAPbI₃ and α-FAPbI₃ perovskite films, respectively. The structures of the mesoscopic TiO₂/perovskite and the perovskite-capping layers between the two SEM micrographs appear indistinguishable. These results confirm the MAPbI₃→α-FAPbI₃ perovskite conversion without degradation in the morphology of the films.

The success of this formylimidamide-gas-induced MAPbI₃→α-FAPbI₃ phase conversion, while preserving the film morphology, may be attributed to the following. With wishing to be bound by theory, first, MAPbI₃ exhibits cubic crystalline structure (space group Pm3m) at elevated temperatures (150° C.) with a lattice parameter of a=6.31 nm, while FAPbI₃ also has a cubic, or a pseudocubic, crystal structure (space group Pm3m or Pm31) with a=6.36 nm. This inherent structural similarity favors MAPbI₃→α-FAPbI₃ conversion. Second, there is a very small difference (˜0.2%) between the densities of MAPbI₃ (4.092 Mg·m⁻³) and α-FAPbI₃ (4.101 Mg·m⁻³), precluding any issues associated with volume change during the MAPbI₃→α-FAPbI₃ conversion. Third, unlike reversible ion-exchange reactions, redox reaction (1) is inherently irreversible, favoring the MAPbI₃→α-FAPbI₃ conversion kinetics. Finally, no solvents were used in reaction (1) precluding any solvent-induced degradation of thin-film morphology. This is in contrast with the solution-based ion-exchange process, which allows compositional tuning of the MAPbI₃-FAPbI₃ perovskite films, but it uses solvents such as isopropanol that can partially dissolve the perovskite, degrading their morphology.

In order to evaluate the quality of the converted α-FAPbI₃ perovskite films, PSCs made from those films (Panel D of FIG. 5) were tested under 1 sun (100 mW·cm⁻²) AM1.5G irradiation. FIG. 6A shows J-V curve for the best PSC showing PCE of 17.9%, along with the extracted PV parameters. Notably, the short-circuit current-density (J_(SC)) of the α-FAPbI₃ PSC shows a high value of 22.8 mA cm⁻², which is clearly attributed to the enhanced absorption in the IR region of the solar spectrum by the α-FAPbI₃ perovskite. FIG. 6B shows the EQE spectrum of the α-FAPbI₃ PSC with J_(SC) of 21.9 mA·cm⁻², which compares favorably to that measured from the J-V curve in FIG. 6A. These results clearly show that the high quality of the original MAPbI₃ perovskite thin-film morphology was preserved in the α-FAPbI₃ perovskite films during the formylimidamide-gas-induced conversion.

Lead iodine acid (HPbI₃) powders were prepared using an anti-solvent vapor-assisted crystallization approach. Briefly, 0.461 g of PbI₂ and 0.224 g of hydroiodic acid (57 wt % in water, unstabilized, Sigma-Aldrich, USA) were mixed and dissolved in 0.493 g of N,N-dimethylformamide (DMF; 99.8%, Sigma-Aldrich, USA) solvent to form a 50 wt % HPbI₃ solution. The as-prepared HPbI₃ solution was then heated at 80° C. in the chlorobenzene (CBE) vapor environment overnight. During the heat-treatment, the CBE molecules diffused into the HPbI₃ DMF solution, which reduced the solubility of HPbI₃. As a result, light yellow, needle-like HPbI₃ crystals are formed. The as-crystallized HPbI₃ solid was then collected and washed, and then dried at 60° C. for 10 hours under vacuum.

Methylamine (CH₃NH₂) gas was synthesized as follows: 10 g CH₃NH₄Cl (98%) and 10 g KOH (85%) powders were sequentially dissolved in 100 mL H₂O and then heated to 60° C. The resulting gas were passed through a CaO dryer to remove any moisture. CH₃NH₂ (anhydrous, 298%) is also commercially available. No obvious difference in the resultant film morphology or device performance was observed when either gas source was used.

To form a uniform highly-crystalline CH₃NH₃PbI₃ (MAPbI₃) film on a substrate, 60 wt % HPbI₃ DMF solution was prepared first using the as-prepared HPbI₃ solids. The solution was then spin-coated on the substrate at 6000 rpm for 20 seconds to form an HPbI₃ film, which was followed by heat-treatment at 150° C. for 30 seconds. Once cooled to the room temperature, the HPbI₃ film was exposed to CH₃NH₂ gas for 2 seconds, and rapidly degassed by removing the gas atmosphere, resulting in a black film. The film was finally heated at 150° C. for 5 minutes.

FIG. 7 illustrates a system 700 used to convert a MAPbI₃ perovskite film 730 to a α-FAPbI₃ perovskite film 730, by heating the as-prepared MAPbI₃ perovskite film 730 at 150° C. for 1 to 5 minutes in an atmosphere of H₂N—CH═NH (formylimidamide) gas. The gas was generated by reacting HC(NH₂)₂CH₃COOH salt (formamidine acetate or FA(Ac)) with NaOH (see reference numeral 750). The resulting gas (not shown) passed through a CaO dryer 740 to remove any moisture. The entire system 700 was enclosed in a gas-tight box 760.

Materials Characterization. X-ray diffraction (XRD) patterns were obtained using an X-ray diffractormeter (D8 Advance, Bruker, Germany) with Cu Kα radiation (λ=1.5406 Å); 0.02° step and 2 s/step dwell. UV-vis absorption spectra of the films were recorded using spectrometer (U-4100, Hitachi, Japan). Surface and cross-sections (fractured) morphology of the perovskite solar cells (PSCs) were observed in a scanning electron microscope (SEM; LEO 1530VP, Carl Zeiss, Germany).

Device Fabrication and Characterization. For the fabrication of the PSCs, a compact TiO₂ electron-transporting layer (ETL) was first deposited on pre-patterned FTO-coated glass (TEC 15, Hartford Glass Co., Hartford City, Ind.) by spray pyrolysis at 450° C. Mesoporous TiO₂ layer was spin-coated at 2000 rpm for 35 seconds from TiO₂ paste, which consists of 5.4% TiO₂ nanoparticles and 1.6% ethyl cellulose in terpineol/ethanol (3/7 weight ratio) solution. The mesoporous layer was sintered at 450° C. for 30 minutes. The perovskite layer was then deposited using the procedure described above. This was followed by spin-coating a hole-transporting material (HTM) solution, which consisted of 80 mg 2,2′,7,7′-tetrakis(N,N-dip-methoxyphenylamine)-9,9′-spirobifluorene (spiro-MeOTAD), 30 μl bis(trifluoromethane) sulfonimide lithium salt stock solution (500 mg Li-TFSI in 1 ml acetonitrile), and 30 μl 4-tert-butylpyridine (TBP), and 1 ml chlorobenzene solvent. The HTM spin-coating process was performed in a dry-air atmosphere with humidity <10%. Finally a 150 nm Ag layer was deposited using thermal evaporator and a shadow mask.

The J-V characteristics of the PSCs were obtained using a 2400 SourceMeter (Keithley, Cleveland, Ohio) under simulated one-sun AM 1.5G illumination (100 mW·cm⁻²) (Oriel Sol3A Class AAA Solar Simulator, Newport Corporation, Irvine, Calif.). Typical J-V scan started from short-circuit to open circuit and then back to short-circuit at the rate of 20 mV·s⁻¹. A typical active area of 0.12 cm² was defined using a non-reflective mask for the J-V measurements. The EQE spectra were recorded at a chopping frequency of 5 Hz in AC mode on a solar cell quantum efficiency measurement system (QEX10, PV Measurements, Boulder, Colo.).

Finally, MAPbI₃ was converted to FAPbI₃ by placing the MAPbI₃ film in formylimidamide gas environment at elevated temperature (e.g., about 160° C.) for a certain period of time (e.g., several minutes). Methyl ammonium was replaced by formamidinium following the aminium displacement reaction shown in reaction (1) above. FIG. 8 shows the absorption spectral evolution of perovskite structure from MAPbI₃ to FAPbI₃ as a function of the reaction time.

EXAMPLES Example 1

A method comprising exchanging at least a portion of a first cation of a perovskite solid with a second cation, wherein the exchanging is performed by exposing the perovskite solid to a precursor of the second cation, such that the precursor of the second cation oxidizes to form the second cation and the first cation reduces to form a precursor of the first cation.

Example 2

The method of Example 1, wherein the exchanging is performed by exposing the perovskite solid to a gas comprising the precursor of the second cation.

Example 3

The method of Example 1, wherein the exchanging is performed by exposing the perovskite solid to a solution comprising the precursor of the second cation.

Example 4

The method of Example 3, wherein the exposing is performed with the gas at a pressure between about 0.1 atmospheres and about 5 atmospheres.

Example 5

The method of Example 4, wherein the pressure is between one atmosphere and two atmospheres.

Example 6

The method of Example 1, wherein the exchanging is performed at a temperature greater than 20° C.

Example 7

The method of Example 6, wherein the temperature is between 100° C. and 300° C.

Example 8

The method of Example 1, wherein the perovskite solid comprises at least one of a particle or a film.

Example 9

The method of Example 8, wherein the film has a thickness between 10 nm and 3 μm.

Example 10

The method of Example 1, wherein the perovskite solid comprises ABX₃, A comprises at least one of the first cation or the second cation, B comprises a third cation, and X comprises an anion.

Example 11

The method of Example 10, wherein the first cation comprises methyl ammonium.

Example 12

The method of Example 10, wherein the second cation comprises at least one of formamidinium, guanidinium, acetamidinium, or ethylammonium.

Example 13

The method of Example 12, wherein the second cation comprises formamidinium.

Example 14

The method of Example 10, wherein the third cation comprises a metal in the 2+ valence state.

Example 15

The method of Example 14, wherein the metal comprises at least one of lead, tin, or germanium.

Example 16

The method of Example 10, wherein the anion comprises a halogen.

Example 17

The method of Example 16, wherein the halogen comprises at least one of fluorine, chlorine, bromine, or iodine.

Example 18

The method of Example 1, wherein the precursor of the second cation comprises at least one of formylimidamide, guanidine, acetamidine, or ethylamine.

Example 19

The method of Example 1, wherein the precursor of the first cation comprises methylammonia.

Example 20

The method of Example 1, wherein the portion is up to and including 100%.

Example 21

The method of Example 1, wherein the perovskite solid is converted from methylammonium lead triiodide to formamidinium lead triiodide.

Example 22

The method of Example 1, further comprising, prior to the exchanging, forming the perovskite solid by at least one of a solution deposition method or a vapor deposition method.

Example 23

The method of Example 2, further comprising producing the gas by reacting a salt-precursor of the precursor of the second cation with a hydroxide salt.

Example 24

The method of Example 23, wherein the salt-precursor of the precursor of the second cation comprises formamidine acetate.

Example 25

The method of Example 24, wherein the hydroxide salt comprises sodium hydroxide.

Example 26

A device comprising a film of formamidinium lead triiodide, wherein the formamidinium lead triiodide has short-circuit density of greater than 22.0 mA/cm².

Example 27

The device of Example 26, wherein the film has thickness between 10 nm and 3 μm.

Example 28

The device of Example 26, further comprising a substrate, wherein the film is in physical contact with the substrate.

Example 29

The device of Example 28, wherein the substrate comprises at least one of at least one of a transparent conducting oxide, a glass, a metal foil, or a plastic.

Example 30

The device of Example 26, wherein the device has a power-conversion efficiency of greater than 17%.

The foregoing discussion and examples have been presented for purposes of illustration and description. The foregoing is not intended to limit the aspects, embodiments, or configurations to the form or forms disclosed herein. In the foregoing Detailed Description for example, various features of the aspects, embodiments, or configurations are grouped together in one or more embodiments, configurations, or aspects for the purpose of streamlining the disclosure. The features of the aspects, embodiments, or configurations, may be combined in alternate aspects, embodiments, or configurations other than those discussed above. This method of disclosure is not to be interpreted as reflecting an intention that the aspects, embodiments, or configurations require more features than are expressly recited in each claim. Rather, as the following claims reflect, inventive aspects lie in less than all features of a single foregoing disclosed embodiment, configuration, or aspect. While certain aspects of conventional technology have been discussed to facilitate disclosure of some embodiments of the present invention, the Applicants in no way disclaim these technical aspects, and it is contemplated that the claimed invention may encompass one or more of the conventional technical aspects discussed herein. Thus, the following claims are hereby incorporated into this Detailed Description, with each claim standing on its own as a separate aspect, embodiment, or configuration. 

1-20. (canceled)
 21. A device comprising a film of formamidinium lead triiodide, wherein the formamidinium lead triiodide has short-circuit density of greater than 22.0 mA/cm².
 22. The device of claim 21, wherein the film has thickness between 10 nm and 3 μm.
 23. The device of claim 21, further comprising a substrate, wherein the film is in physical contact with the substrate.
 24. The device of claim 23, wherein the substrate comprises at least one of at least one of a transparent conducting oxide, a glass, a metal foil, or a plastic.
 25. The device of claim 21, wherein the device has a power-conversion efficiency of greater than 17%.
 26. A composition comprising: a final perovskite comprising ABX₃, wherein: A comprises a first cation, B comprises a second cation, and X comprises an anion, A results from the exchange of a third cation of a starting perovskite comprising A′BX₃, where A′ is the third cation, with the first cation, and the exchange results from the exposing of the starting perovskite to a gas comprising a precursor of the third cation. 